Solid State Properties Of Polyethylene Prepared With Tetrahydroindenyl-Based Catalyst System

ABSTRACT

The present invention discloses articles having excellent dimensional stability, solid state mechanical properties and barrier properties that are produced with a polyethylene resin prepared with a catalyst system based on a bridged bisindenyl ligand.

This invention relates to the field of polyethylene prepared with acatalyst system based on a tetrahydroindenyl catalyst component and totheir solid state properties.

Rotomoulding is used for the manufacture of simple to complex, hollowplastic products. It can be used to mould a variety of materials such asfor example polyethylene, polypropylene, polycarbonate or polyvinylchloride (PVC). Polyethylene (PE) represents more than 80% of thepolymers used in the rotomoulding market. This is due to the outstandingresistance of polyethylene to thermal degradation during processing, toits easy grinding, good flowability, and low temperature impactproperties.

Polyethylenes prepared with a Ziegler-Natta catalyst are generally usedin rotomoulding, but metallocene-produced polyethylenes are desirable,because their narrow molecular weight distribution allows better impactproperties and shorter cycle time in processing.

Most of the metallocene-prepared polyethylene resins available on themarket (see ANTEC, vol. 1, 2001) are prepared with a catalyst systembased on bis(n-butyl-cyclopentadienyl) zirconium dichloride. They sufferfrom poor dimensional stability such as high shrinkage and warpage. Theyalso suffer from creep or permanent deformation under stress.

Godinho et al. (in Polymers, Rubbers and Composites, vol 29, n^(o)7, pp316, 2000) have shown that for semi-crystalline polymers such aspolyethylene small spherulite size equivalent to fine microstructureprovides improved dimensional stability as well another solid stateproperties such as for example improved impact strength.

It is an aim of the present invention to provide polyethylene resinshaving a fine microstructure that can be tailored according to needs.

It is also an aim of the present invention to provide polyethyleneresins having reduced shrinkage.

It is another aim of the present invention to provide polyethyleneresins having reduced warpage.

It is a further aim of the present invention to provide polyethyleneresins having high creep resistance.

It is a yet further aim of the present invention to provide apolyethylene resin having high impact resistance.

It is yet another aim of the present invention to provide a polyethyleneresin having high stress crack resistance.

It is also an aim of the present invention to provide a polyethyleneresin having excellent barrier properties.

Accordingly, the present invention discloses a method for preparing ahomopolymer or a copolymer of ethylene that comprises the steps of:

a) Injecting into the reactor a catalyst system comprising i) ametallocene catalyst component of general formula I

R″(Ind)₂MQ₂  (I)

wherein (Ind) is an indenyl or an hydrogenated indenyl, substituted orunsubstituted, R″ is a structural bridge between the two indenyls toimpart stereorigidity that comprises a C₁-C₄ alkylene radical, a dialkylgermanium or silicon or siloxane, or a alkyl phosphine or amine radical,which bridge is substituted or unsubstituted; Q is a hydrocarbyl radicalhaving from 1 to 20 carbon atoms or a halogen, and M is a transitionmetal Group 4 of the Periodic Table or Vanadium, ii) an activating agentand iii) optionally a support;b) injecting into the reactor ethylene monomer at a concentration of atleast 6.5 wt %,c) injecting an amount of hydrogen such that the ratio H₂/C₂ in the feedis of less than 85 g/10⁶ g;d) maintaining under polymerisation conditions at a temperature of lessthan 90° C.;e) retrieving polyethylene resin that is suitable for preparing articleshaving excellent solid state and barrier properties.

Each indenyl or hydrogenated indenyl compound may be substituted in thesame way or differently from one another at one or more positions in thecyclopentadienyl ring, the cyclohexenyl ring and the bridge.

Each substituent on the indenyl may be independently chosen from thoseof formula XR_(v) in which X is chosen from Group 14 of the PeriodicTable, oxygen and nitrogen and each R is the same or different andchosen from hydrogen or hydrocarbyl of from 1 to 20 carbon atoms and v+1is the valence of X. X is preferably C. If the cyclopentadienyl ring issubstituted, its substituent groups must not be so bulky as to affectcoordination of the olefin monomer to the metal M. Substituents on thecyclopentadienyl ring preferably have R as hydrogen or CH₃. Morepreferably, at least one and most preferably both cyclopentadienyl ringsare unsubstituted.

In a particularly preferred embodiment, both indenyls are unsubstituted,and most preferably they are unsubstituted hydrogenated indenyls.

The active catalyst system used for polymerising ethylene comprises theabove-described catalyst component and a suitable activating agenthaving an ionising action.

Suitable activating agents are well known in the art.

Optionally, the catalyst component can be supported on a support.

The polymerisation conditions necessary to obtain the desiredpolyethylene resin comprise a high concentration of ethylene, little orno hydrogen and a low polymerisation temperature. The concentration ofethylene is of at least 6.5 wt %, preferably of at least 7 wt %. Theamount of hydrogen is selected to give a H₂/C₂ in the feed of at most 85g/10⁶ g, preferably of at most 60 g/10⁶ g, more preferably there is nohydrogen. The polymerisation temperature is of less than 90° C.,preferably of less than 88° C., more preferably of from 80 to 85° C.

The PE resins prepared with the metallocene catalyst system of thepresent invention may be homo- or co-polymers of ethylene with densitiesranging from 0.930 to 0.965 g/cc. The density is measured following themethod of standard test ASTM 1505 at a temperature of 23° C. The meltindex is typically of at least 0.5, preferably of at least 3, asmeasured following the method of standard test ASTM D 1238 under a loadof 2.16 kg and at a temperature of 190° C. They are characterised by anarrow molecular weight distribution, typically with a polydispersityindex (D) lower than 3. The polydispersity index is defined as the ratioMw/Mn of the weight average molecular weight Mw to the number averagemolecular weight Mn. The long Chain Branching Index (LCBI) is superiorto 0, indicating the presence of long chain branching. It issurprisingly observed that the long chain branching (LCB) initiates anauto-nucleation process. The magnitude of this nucleation processincreases with increasing long chain branching and LCB itself can betailored by modifying the polymerisation conditions. Thisauto-nucleation process suppresses or reduces the need for externalnucleating agents for polyethylene resins.

These polyethylene resins can be used to prepare articles by all methodsgenerally used in the field, such as for example rotomoulding, injectionmoulding, blow moulding or extrusion. They are particularly advantageousin rotomoulding applications.

The finished articles according to the present invention have severalattractive properties.

-   -   They have a very fine microstructure characterised by an average        spherulite diameter, smaller than those prepared either with        Ziegler-Natta (ZN) resins or resins prepared with other        metallocene catalyst systems. The copolymers of ethylene        obtained according to the present invention have a typical        spherulite size of less than 20 μm, preferably of less than 18        μm.    -   They have excellent properties in the solid state such as        -   i) mechanical properties,        -   ii) barrier properties,        -   iii) dimensional stability.

The barrier properties of articles prepared with the resins according tothe invention are of less than 1 g/day, preferably of less than 0.5g/day.

These properties will be illustrated by way of examples.

LIST OF FIGURES

FIG. 1A to 1J represent the microstructure measured on 700 mLrotomoulded bottles prepared respectively with resins R1 to R10.

FIG. 2 represents the true deformation expressed in cm as a function oftime expressed in weeks for resins R7, R8 and R9. In this figure, thestar for resin R8 indicates breakage.

FIG. 3 represents the true deformation expressed in cm as a function oftime expressed in weeks for resins R3, R4 and R6.

FIG. 4 represents the true longitudinal deformation expressed in mm as afunction of time expressed in seconds in traction creep tests carriedout at a temperature of 80° C. with applied stresses of 14 to 18 MPa onrotomoulded parts prepared respectively with resins R4 and R6.

FIG. 5 represents the true longitudinal deformation expressed in mm as afunction of time expressed in seconds in traction creep tests carriedout at room temperature with an applied stress of 16 MPa on rotomouldedparts prepared respectively with resins R3 and R6.

FIG. 6 represents the long branching index LCBI as a function ofspherulite size expressed in μm.

FIG. 7 represents the spherulite size expressed in μm as a function ofmelt index MI2 expressed in dg/min.

FIG. 8 represents the LCBI as a function of melt index MI2 expressed indg/min.

FIGS. 9 a, 9 b and 9 c represent the load displacement curves at atemperature of −40° C. for 4.5 mm thick rotomoulded articles preparedrespectively with resins R6, R3 and R4. The load is expressed in Newtonsand the displacement in mm.

EXAMPLES

Several polyethylene resins have been used to prepare respectively

-   -   700 mL rotomoulded bottles, using an proprietary mould;    -   10 L rotomoulded bottles, using an proprietary mould;    -   tanks;    -   32 mm diameter tubes, using an proprietary mould;    -   moulded samples; and    -   powder samples

Resin R1 is a Ziegler-Natta (ZN) PE resin sold by Exxon Mobill Chemicalsunder the name LX0210.

Resin R2 is a ZN PE resin sold by Matrix under the name N307.

Resin R3 is a ZN PE resin sold by Dow Chemicals under the name NG2432.

Resin R4 is a metallocene-prepared PE resin sold by Borealis under thename

RM7402. Resin R5 is a ZN PE resin sold by Borealis under the nameRG7403.

Resin R6 is a resin according to the present invention prepared with abridged bis(tetrahydroindenyl)-based catalyst system.

Resin R7 is a metallocene-prepared PE sold by Borealis under the nameRM8403.

Resin R8 is a ZNPE resin sold by Dow Chemicals under the name NG2431.

Resin R9 is a resin according to the present invention prepared with abridged bis(tetrahydroindenyl)-based catalyst system.

Resin R10 is a resin according to the present invention prepared with abridged bis(tetrahydroindenyl)-based catalyst system.

Resin R11 is a homopolymer of ethylene according to the presentinvention prepared with a bridged bis(tetrahydroindenyl)-based catalystsystem.

Their properties are summarised in Table I.

TABLE I MI2 Density Tm Spherul. Size Dg/min g/cc ° C. LCBI μm R1 4.150.941 127.5 0 27.55 R2 3.77 0.941 126.5 0 21.48 R3 3.64 0.940 127 020.18 R4 3.98 0.940 127.5 0 19.82 R5 3.83 0.944 127.5 0 20.81 R6 3.80.940 126 0.6 14.4  R7 6 0.934 0 37.6  R8 7 0.935 0 30.7  R9 8 0.934 0.316   R10 0.9 0.934 1.6 8   R11 7.39 0.960 137 0.14 22*   *It must benoted that the spherulite size increases with increasing density andthat for the density of 0.960 g/cc of resin R11, the observed spherulitesize is extremely small.

The melt flow index MI2 was measured following the method of standardtest ASTM D 1238, under a load of 2.16 kg and at a temperature of 190°C. The density was measured following the method of standard test ASTM D1505 at a temperature of 23° C.

The spherulite size is measured by Small Angle Light Scattering (SALS).When a beam of light passes through a thin slice of a semi-crystallinepolymer, which is positioned between two crossed polarisers, thespherulites of the polymer diffuse the light and a four-leaf pattern isprojected onto a screen positioned after the second polariser. The sizeof the pattern is inversely related to the spherulite diameter and maybe used for its determination.

Rigidity analyses were carried out as follows.

The Young modulus was measured on compression-moulded samples followingthe method of standard test ASTM D 790 on samples R3 and R6 having anidentical density. The Young modulus of resin R6 was higher than that ofprior art resin R3 with values respectively of 575 MPa for resin R3 andof 615 Mpa for resin R6.

Rheological dynamic analysis in torsion mode was carried out on powdersamples for resins R3 and R6, and in tensile mode for resins R1, R3, R4,R5 and R6. The elastic modulus E′ (tensile mode) of resins according tothe present invention had a higher value than that of all prior artresins over the whole range of tested temperatures.

Dynamic mechanical analysis measurements were carried out on 700 mLrotomoulded bottles prepared with a Peak Internal Air Temperature (PIAT)of 230° C. Compression tests were carried out to determine the forcenecessary to achieve for a 5 mm displacement and the maximum force forseveral resins. The resins according to the present inventionoutperformed all other resins.

Tensile analysis was carried out on rotomoulded tanks using the methodsof standard test ISO R527/sample type 5, at a temperature of 23° C. andat a stretching speed of 100 mm/min. Resin R6 had a behaviour similar toor slightly better than that of the prior art resins for the yieldstress, the Young's modulus and the elongation at break.

The resistance to impact was tested by the falling weight method onrotomoulded tanks and by the drop test on 10 L rotomoulded bottleshaving a 6 mm wall thickness.

The resins according to the present invention were all less brittle thanthe prior art resins.

The drop test was carried out at a temperature of −18° C., on 10 Lrotomoulded bottles having a wall thickness of 6 mm and prepared with aproprietary mould. The bottles were dropped from increasing heightsuntil failure occurred.

Prior art resin R1 failed at a height of 1.5 m.

Prior art resin R4 failed at a height of 2 m.

Prior art resin R5 failed at a height of 6 m.

Resin R6, according to the present invention did not fail up to a heightof 6.5 m both at a temperature of −18° C. and at a temperature of −40°C.

All resins were also tested for stacking on 700 mL rotomoulded bottles,prepared with a proprietary mould, filled with a wetting agent (Huperolat 5% in water) and placed under a load of 35 kg. The height of thebottles was measured before loading and then at different time intervalsafter loading. The results are summarised in Table II.

TABLE II bottle weight bottle height (mm) Resin (g) t = 0 t = 24 h t =72 h t = 1 wk t = 2 wk t = 5 wk t = 8 wk R2 78.95 212 208 198.5 broken —— — R3 79.2 212.25 209.75 204.25 203.25 201 broken — R4 78.825 212 209203.75 204 204 broken — R5 78.55 212 208.5 broken — — — — R6 78.65 211208.5 201.5 199.75 200 201 broken

In this table, the term “broken” means that, at least 50% of the testedsamples, broke during the test.

From Table II it appears that the polyethylene resin of the presentinvention exhibits an excellent performance in the stacking test.

The stacking test performed at a temperature of 40° C. on 700 mLrotomoulded bottles having a 2.5 mm wall thickness, prepared with resinsR7, R8 and R9 with a proprietary mould, filled with a wetting agent(Huperol at 5% in water) and placed under a load of 40 kg are displayedin FIG. 2 representing the deflection expressed in cm as a function oftime expressed in days.

The stacking test performed at a temperature of 40° C. on 700 mLrotomoulded bottles having a 1.5 mm wall thickness, prepared with resinsR3, R4 and R6 with a proprietary mould, filled with HNO₃ (55%) andplaced under a load of 35 kg are displayed in FIG. 3 representing thedeflection expressed in cm as a function of time expressed in days.

The environmental stress crack resistance (bottle ESCR) tests wereperformed on 700 mL rotomoulded bottles having a 1.5 mm wall thickness,prepared with a proprietary mould and filled with an Antarox 10%solution. They were submitted to a force of 6 newtons per cm² at atemperature of 60° C. The resin according to the present inventionoutperformed all other resins as can be seen in Table III.

TABLE III Resin R1 R3 R4 R5 R6 ESCR (hr) 26 40 48 19 54

Creep tests were also carried out. Results for the true longitudinaldeformation as a function of time, for tubes submitted to a tractioncreep of 16 Mpa at room temperature are exhibited in FIG. 4 for resinsR8 and R9 and in FIG. 5 for resins R3 and R6. They show the improvedbehaviour of resins R9 and R6 according to the present invention.

Pressure tests were carried out on rotomoulded pipes having a 32 mmdiameter and a 3 mm wall thickness. They were submitted to a pressure of3.5 Mpa at a temperature of 80° C. Prior art resin R3 failed after aperiod of time of 50 hours as compared to resin R6 according to thepresent invention that failed after a period of time of 400 hours.

Barrier properties were studied on rotomoulded 10 L bottles having awall thickness of 6 mm and prepared with a proprietary mould. They werefilled with fuel (CEC RF08-A-85 according to norm Standard ECE34-annex5) at a temperature of 40° C. The results for the permeability to fuel,expressed in g/day, displayed in Table IV clearly show the outstandingbarrier properties of resins R6 and R11.

TABLE IV Resin R2 R3 R4 R5 R6 R11 Permeability 2.6 1.17 0.771 2.1 0.4570.097 (g/day)

It can be seen that the resins according to the present inventionclearly outperform all prior art resins with permeabilities of less than0.5 g/day.

In addition, and quite contrary to prior art resins, clear correlationswere observed between the long chain branching index LCBI, thespherulite size and the melt index. This behaviour is summarisedrespectively in FIGS. 6 to 8. FIG. 6 shows a linear correlation betweenthe LCBI and the spherulite size. The spherulite size decreased linearlywith increasing LCBI for resins R6, R9 and R10 whereas it remainedunchanged for prior art resins. FIG. 7 shows a correlation between LCBIand melt index MI2 for the resins according to the present invention.The melt index increased with decreasing LCBI. In the resins of thepresent invention, the LCB content could thus be tailored by modifyingthe melt index. FIG. 8 shows a linear correlation between the melt indexand the spherulite size. The melt index increased linearly withincreasing spherulite size.

Impact tests were performed on rotomoulded articles preparedrespectively with resin R6 according to the present invention and resinsR3 and R4 usually employed in the field. The tests were performedfollowing the method of standard test ISO 6603-2, respectively attemperatures of 20° C., −20° C. and −40° C. and on samples having athickness of 4.5 and 6 mm. The results are displayed in Table V.

TABLE V Thickness Temperature Peak Load Peak Energy Total Energy Resin(mm) (° C.) (kN) (J) (J) R6 4.5  20 5.47 44.5 129.9 R3 5.5 46.7 104.9 R45.89 48.9 89.7 R6 6.0 8.6 102.5 252.8 R3 6.62 55.9 118.6 R4 8.81 90.1279.5 R6 4.5 −20 7.32 63.2 188.6 R3 4.43 16.8 25.7 R4 5.94 31.8 74.0 R66.0 11.13 127.5 314.5 R3 4.74 15.1 25.2 R4 11.2 113.1 295 R6 4.5 −407.99 66.1 178.4 R3 2.38 4.3 11.7 R4 6.38 31.8 58.4 R6 6.0 12.11 125.2334.3 R3 4.04 7.7 14.8 R4 10.46 92.4 235.5

Resin R6 according to the present invention outperforms the other resinsat all tested temperatures.

The load displacement curves, at a temperature of −40° C., are presentedon FIGS. 9 a, 9 b and 9 c for the 4.5 mm rotomoulded samples preparedrespectively with resins R6, R3 and R4.

Resin R6 exhibits a pure ductile behaviour at all tested temperatures,contrary to the other tested resins.

In addition a falling weight impact test was also carried out at atemperature of −20° C. on a 10 litres rotomoulded bottles having a wallthickness of 6 mm and prepared with resin R11. The bottles all had acompletely ductile behaviour and the impact results are summarised inTable VI.

TABLE VI Total Energy J Speed m/s Maximum Energy J 107.03 3.34 66.2126.03 3.09 68.44 72.15 3.73 37.44 119.97 3.17 81.02 94.76 3.48 61.65

All the articles prepared according to the present invention also hadoutstanding optical properties.

In conclusion, for all the tests performed, the polyethylene resinaccording to the present invention proved at least as good as and inmost instances far better than all the prior art resins.

The same conclusions apply to articles prepared using other methods thanrotomoulding such as for examples extrusion, injection moulding, slushmoulding or thermoforming.

1. A method for preparing a homopolymer or a copolymer of ethylene that comprises the steps of: a) Injecting into the reactor a catalyst system comprising i) a metallocene catalyst component of general formula I R″(Ind)₂MQ₂  (I) wherein (Ind) is an indenyl or an hydrogenated indenyl, substituted or unsubstituted, R″ is a structural bridge between the two indenyls to impart stereorigidity that comprises a C₁-C₄ alkylene radical, a dialkyl germanium or silicon or siloxane, or a alkyl phosphine or amine radical, which bridge is substituted or unsubstituted; Q is a hydrocarbyl radical having from 1 to 20 carbon atoms or a halogen, and M is a transition metal Group 4 of the Periodic Table or Vanadium, ii) an activating agent and iii) optionally a support; b) injecting into the reactor ethylene monomer at a concentration of at least 6.5 wt %; c) injecting an amount of hydrogen such that the ratio H₂/C₂ in the feed is of less than 85 g/10⁶ g; d) maintaining under polymerisation conditions at a temperature of less than 90° C.; e) retrieving polyethylene resin.
 2. The method according to claim 1 wherein, in the metallocene component, both indenyls are unsubstituted.
 3. The method according to claim 2 wherein both unsubstituted indenyls are tetrahydroindenyls.
 4. The method according to any one of claims 1 to 3 wherein the concentration in ethylene in the polymerisation reactor is larger than 7 wt %.
 5. The method according to any one of the preceding claims wherein the amount of hydrogen in the polymerisation reactor is selected to give a C₂/H₂ ratio of less than 60 g/10⁶ g.
 6. The method according to any one of the preceding claims wherein the polymerisation temperature is of less than 88° C.
 7. The method according to any one of the preceding claims to produce a polyethylene resin that auto-nucleates.
 8. Use of the polyethylene resin prepared by the method according to any one of the preceding claims to produce finished articles having excellent solid state and barrier properties by rotomoulding, injection moulding, extrusion, thermoforming or slush moulding.
 9. Rotomoulded articles having a permeability of less than 1 g/day obtainable by the method of any one of claims 1 to
 7. 10. A method for preparing a homopolymer or a copolymer of ethylene that comprises the steps of: a) Injecting into the reactor a catalyst system comprising i) a metallocene catalyst component of general formula I R″(Ind)₂MQ₂  (I) wherein (Ind) is an indenyl or an hydrogenated indenyl, substituted or unsubstituted, R″ is a structural bridge between the two indenyls that comprises a C₁-C₄ alkylene radical, a dialkyl germanium or silicon or siloxane, or a alkyl phosphine or amine radical, which bridge is substituted or unsubstituted; Q is a hydrocarbyl radical having from 1 to 20 carbon atoms or a halogen, and M is a transition metal Group 4 of the Periodic Table or Vanadium and ii) an activating agent; b) injecting into the reactor ethylene monomer at a concentration of at least 6.5 wt %; c) injecting an amount of hydrogen such that the ratio H₂/C₂ in the feed is of less than 85 g/10⁶ g; d) maintaining under polymerisation conditions at a temperature of less than 90° C.; and e) retrieving polyethylene.
 11. The method according to claim 10 wherein, in the metallocene component, both indenyls are unsubstituted.
 12. The method according to claim 11 wherein both unsubstituted indenyls are tetrahydroindenyls.
 13. The method according to claim 10 wherein the concentration of ethylene in the polymerization reactor is larger than 7 wt %.
 14. The method according to claim 10 wherein the amount of hydrogen in the polymerization reactor is selected to give a C₂/H₂ ratio of less than 60 g/10⁶ g.
 15. The method according to claim 10 wherein the polymerisation temperature is less than 88° C.
 16. The method according to claim 10 wherein the polyethylene is capable of auto-nucleation.
 17. Rotomoulded articles having a permeability of less than 1 g/day comprising polyethylene obtained by the method of claim
 10. 